THERMOTROPIC POLY(ESTERAMIDE)S CONTAINING MONOMER UNITS DERIVED FROM 4,4'-BIPHENYLDICARBOXYLIC ACID

Abstract: Thermotropic aromatic liquid crystalline poly(esteramide)s comprise monomer units A, B, C and D, where A is the dioyl residue of 4,4'-biphenyldicarboxylic acid and optionally one or more other aromatic diacids; B is the dioxy residue of one or more aromatic diols; C is the oxyaroyl residue of 4-hydroxybenzoic acid, 6-hydroxy-2-naphthoic acid, or a mixture thereof; and D is derived from 4-aminophenol, 4-aminobenzoic acid, p-phenylenediamine, or 3-aminophenol.

Description: THERMOTROPIC POLY(ESTERAMIDE)S CONTAINING MONOMER UNITS DERIVED FROM 4,4'-BIPHENYLDICARBOXYLIC ACID Field of the Invention This invention relates generally to thermotropic liquid crystalline polymers, and more specifically to thermotropic liquid crystalline poly(esteramide)s that contain 4,4'- biphenyldicarboxylic acid. Background of the Invention Thermotropic liquid crystalline polymers are a well known class of polymeric materials. They have high thermal stability and excellent mechanical properties when they are shaped into such articles as fibers, films and molded parts. Several thermotropic liquid crystalline polymer compositions are manufactured and sold commercially. There is a continuing need for new liquid crystalline polymers that have higher thermal properties, impact strength, and tensile properties and that are readily processed in the melt without extensive decomposition. Thermotropic liquid crystalline polymers that contain monomer units derived from 4,4'-biphenyldicarboxylic acid are known but have not been investigated as thoroughly as compositions containing other monomer units. For example, polyesters containing this monomer unit have been reported in U. S. Patent Nos. 5,055,546, 5,071,942 and 5,250,654. There are also numerous thermotropic poly(esteramide) compositions, such as those reported in U. S. Patent Nos. 5,204,443, 4,330,457, 4,966,956, 4,355,132, 4,339,375, 4,351,917 and 4,351,918. However, it appears that there are no reports of poly(esteramide)s that contain monomer units derived from 4,4'- biphenyldicarboxylic acid and aromatic amines. Summary Of the Invention Thermotropic liquid crystalline poly(esteramide)s have now been found that comprise monomer units A, B, C, and D, where A is and optionally the dioyl residue of one or more other aromatic diacids; B is the dioxy residue of one or more aromatic diols; C is the oxyaroyl residue of 4-hydroxybenzoic acid, 6-hydroxy-2-naphthoic acid, or a mixture thereof; and D is one or more of the following monomer units: In the formula for D, R and R' can be alike or different, and each can be H, C, to C 4 alkyl, or phenyl, with the C, to C 4 alkyl groups optionally being substituted with Cl, F, and mixtures thereof. If R or R' is phenyl, it may also be substituted with Cl, F, C, to C 4 alkyl, and mixtures thereof. Furthermore, some or all of the aromatic groups of monomer units A, B, C, and D may optionally be substituted with one or more of the following moieties: F, Cl, Br, I, and C, to C 4 alkyl groups which may be partially or fully substituted with Cl, F, or mixtures of Cl and F. This poly(esteramide) comprises on a molar basis about 1 to about 45% of monomer unit A, about 1 to about 45% of monomer unit B, about 10 to about 95% of monomer unit C, and about 1 to about 30% of monomer unit D. The thermotropic poly(esteramide) is capable of forming a liquid crystalline melt at a temperature that is greater than or equal to about 200°C and less than or equal to about 400 C C. These thermotropic poly(esteramide)s are readily processed in the melt to yield fibers having high modulus and strength. They are also readily injection molded to yield shaped articles having excellent tensile properties, flexural properties, and impact properties, as shown by a high notched Izod impact strength. The molded and shaped articles also have excellent thermal stability, as demonstrated by a high heat distortion temperature under load. Detailed Description Of The Invention In preferred embodiments, A is the dioyl residue of 4,4'-biphenyldicarboxylic acid, i.e. and may also include the dioyl residue of one or more optional other diacids selected from terephthalic acid, isophthalic acid, 2,6-naphthalenedicarboxylic acid, and 2,7- naphthalenedicarboxylic acid. Monomer unit B is the dioxy residue of one or more of the following diols: 1,4-hydroquinone, 4,4'-biphenol, 2,6-dihydroxynaphthalene, and 2,7-dihydroxynaphthalene. Preferably, monomer unit C is the oxyaroyl residue of 4- hydroxybenzoic acid or is a mixture of the oxyaroyl residues of 4-hydroxybenzoic acid (i.e., 4-oxybenzoyl) and 6-hydroxy-2-naphthoic acid (i.e., 6-oxy-2-naphthoyl), where the amount of 6-oxy-2-naphthoyl comprises up to about 15 mole % of the aromatic poly(esteramide). Preferably monomer unit D is the esteramide monomer unit that is derived from 4-aminophenol, i.e., Preferred thermotropic poly(esteramide)s comprise on a molar basis about 3 to about 30% of monomer unit A, about 3 to about 30% of monomer unit B, about 40 to about 90% of monomer unit C, and about 1 to about 20% of monomer unit D. In more preferred embodiments, the thermotropic aromatic poly(esteramide) comprises on a molar basis about 10 to about 30% of monomer unit A, about 5 to about 25% of monomer unit B, about 50 to about 80% of monomer unit C, and about 5 to about 15% of monomer unit D. In the descriptions of polymer compositions recited above and elsewhere, monomer units are expressed as a mole % of the entire polymer composition, and quantities of monomers used in their preparation are expressed as a mole % of all the monomers used in making the polymer, unless otherwise stated. As previously stated, the compositions taught herein yield a liquid crystalline melt at some temperature in the range of about 200°C to about 400°C. More preferred polymers have a melting point at some temperature in the range of about 250 °C to about 375°C. Highly preferred polymers comprise monomer units A, B, C, and D, where A is 4,4'-biphenyldicarbonyl, which is and optional terephthaloyl, with the terephthaloyl comprising up to about 25 mole % of the polymer. Monomer unit B is the dioxy residue of 4,4'-biphenol, alone or in combination with up to about 20 mole % of the dioxy residue of 1 ,4-hydroquinone, expressed as a mole % of the polymer. Monomer unit C in this composition is 4- oxybenzoyl and optional 6-oxy-2-naphthoyl, where the amount of 6-oxy-2-naphthoyl comprises up to abut 15 mole % of the polymer. Monomer unit D is the esteramide residue of 4-aminophenol. Finally, specific compositions have been found to have an excellent combination of properties, when molded into test specimens containing glass fiber. One specific polymer comprises monomer units A, B, C, and D, where monomer unit A is a mixture of and terephthaloyl, each at a level of about 2 to about 25 mole % of the polymer; monomer unit B is the dioxy residue of 4,4'-biphenol; monomer unit C is 4-oxybenzoyl; and monomer unit D is the esteramide residue of 4-aminophenol. These polymers have an excellent combination of tensile properties, flexural properties, and impact properties (notched Izod) when they are filled with 30% by weight of glass fiber and are injection molded. Another highly desirable polymer comprises monomer units A, B, C, and D, where monomer unit A is monomer unit B is the dioxy residue of 4,4'-biphenol; monomer unit C comprises about 35 to about 78 mole % of 4-oxybenzoyl and about 2 to about 15 mole % of 6-oxy-2- naphthoyl, expressed as a mole % of the polymer; and monomer unit D is the esteramide residue of 4-aminophenol. This polymer also has excellent tensile and flexural properties when it is filled with 30% glass fiber and injection molded. The invention also comprises a method of synthesizing a thermotropic aromatic poly(esteramide) which forms a liquid crystalline melt at some temperature in the range of about 200°C to about 400°C. In this method, monomers A, B, C, and D are condensed in the following amounts on a mole basis: about 1 to about 45% each of monomers A and B, about 10 to about 95% of monomer C, and about 1 to about 30% of monomer D. Monomer A is 4,4'-biphenyldicarboxylic acid and optionally one or more aromatic diacids selected from the group consisting of terephthalic acid, isophthalic acid, 2,6-naphthalenedicarboxylic acid, and 2,7-naphthalenedicarboxylic acid, or reactive derivatives thereof. Monomer B is one or more aromatic diols selected from the group consisting of 1,4-hydroquinone, 4,4'-biphenol, 2,6-dihydroxynaphthalene and 2,7-dihydroxynaphthalene, or reactive derivatives thereof. Monomer C is 4- hydroxybenzoic acid, 6-hydroxy-2-naphthoic acid, or a mixture of the two hydroxyacids, including reactive derivatives. Monomer D is one or more aromatic hydroxyamines or reactive derivatives thereof, selected from the group consisting of where R and R' are alike or different and are selected from the group consisting of H, C, to C 4 alkyl and phenyl. The C, to C 4 alkyl group is optionally substituted with Cl, F or mixtures thereof. The phenyl is optionally substituted with Cl, F, C, to C 4 alkyl and mixtures thereof. Some or all of the aromatic groups of the monomers A, B, C, and D may optionally be substituted with F, Cl, Br, I, and C, to C 4 alkyl groups that may optionally be partially or fully substituted with Cl , F, and mixtures thereof. Monomers A, B, C and D are condensed to yield a poly( esteramide) having an inherent viscosity of at least about 3.0 dl/g, and preferably about 5 dl/g, when measured at about 25°C as a 0.1% solution on a weight/volume basis in a mixture of equal volumes of pentafluorophenol and hexafluoroisopropanol. In a preferred method of synthesizing a thermotropic aromatic poly(esteramide), monomer C is 4-hydroxybenzoic acid, optionally containing up to about 15 mole % of 6-hydroxy-2-naphthoic acid, expressed as a mole % of all the monomers, and monomer D is 4-aminophenol. Reactive derivatives of these monomers may also be used. The aromatic poly(esteramide) is made by condensing on a mole basis about 3 to about 30% each of monomers A and B, about 40 to about 90% of monomer C, and about 1 to about 20% of monomer D. More preferably, the aromatic poly(esteramide) is made by condensing on a mole basis about 10 to about 30% of monomer A, about 5 to about 25% of monomer B, about 50 to about 80% of monomer C, and about 5 to about 15 % of monomer D. More preferred polymers are made by condensing monomers A, B, C, and D, or reactive derivatives thereof, where A is 4,4'-biphenyldicarboxylic acid, optionally including up to about 25 mole % terephthalic acid, expressed as a mole % of all the monomers; B is 4,4'-biphenol, optionally including up to about 20 mole % of 1,4- hydroquinone, expressed as a mole % of all the monomers; C is 4-hydroxybenzoic acid, optionally including up to about 15 mole % of 6-hydroxy-2-naphthoic acid, expressed as a mole % of all the monomers; and D is 4-aminophenol. A highly preferred aromatic poly(esteramide) with excellent properties is made by condensing monomers A, B, C, and D, or reactive derivatives thereof, where A comprises about 2 to about 25 mole % each of 4,4'-biphenyldicarboxylic acid and terephthalic acid expressed as a mole % of all the monomers; B is 4,4'-biphenol; C is 4- hydroxybenzoic acid; and D is 4-aminophenol. Another highly preferred polymer is made by condensing monomers A, B, C, and D, or reactive derivatives thereof, where A is 4,4'-biphenyldicarboxylic acid; B is 4,4'-biphenol; C comprises about 35 to about 78 mole % of 4-hydroxybenzoic acid and about 2 to about 15 mole % of 6-hydroxy-2- naphthoic acid, expressed as a mole % of all the monomers; and D is 4-aminophenol. The condensation step referred to above can be carried out according to any of the methods commonly used in the art, including the following: interfacial polymerization; the reaction of preformed phenyl esters of the aromatic acid groups with the phenolic groups to yield polyester linkages and by-product phenol; and melt acidolysis polymerization, which is the preferred method. All of these polymerization methods involve the condensation of reactive derivatives of the monomers rather than the free monomers, since the aromatic phenols and acids do not polymerize well. In melt acidolysis polymerization, the phenolic reactants are acetylated to yield phenyl acetate groups, and these are then heated in the melt with the aromatic acids to yield acetic acid and polyester linkages. This method is described in numerous patents including U. S. Patent No. 4,473,682. The melt acidolysis method is most conveniently carried out by combining the reactants with acetic anhydride to acetylate the phenolic groups of the reactants in situ and then heating the acetylated monomers to a high enough temperature to induce polymerization. The melt acidolysis method is also useful for aromatic amines, which are generally charged to the reaction as N-acetyl derivatives rather than being acetylated in situ. Thus, the preferred aromatic amine, 4-aminophenol, is generally charged to the polymerization reaction as N-acetyl-4-aminophenol (also referred to as 4-hydroxyacetanilide). Examples of methods of synthesizing aromatic poly(esteramide)s by this method can be found in numerous references, such as U. S. Patent Nos. 5,204,443, 4,330,457, 4,966,956, 4,355,132, 4,339,375, 4,351,917 and 4,351,918. The polymerization reaction is carried out until the polymer reaches a useful molecular weight, as indicated by the inherent viscosity measured at 25°C of a 0.1% solution on a weight/volume basis in a mixture of equal volumes of pentafluorophenol and hexafluoroisopropanol. The inherent viscosity of the polymer is at least about 3.0 dl/g, and preferably at least about 5 dl/g. The polymers made according to this invention are useful as shaped articles, such as fibers, films and molded articles. When the thermotropic poly(esteramide)s are used as resins for injection molding, they are generally blended with fillers and other additives at levels up to about 70% by weight in order to achieve optimum properties. Fillers and additives that may be useful include one or more fillers or reinforcing agents selected from the following list, which is not a complete or exhaustive list: glass fiber, calcium silicate, silica, clays, talc, mica, polytetrafluoroethylene, graphite, alumina trihydrate, sodium aluminum carbonate, barium ferrite, wollastonite, carbon fiber, polymeric fiber, aluminum silicate fiber, titanium fiber, rock wool fiber, steel fiber, tungsten fiber, and wollastonite fiber. Other kinds of additives that may be used in addition to fillers and reinforcing agents include oxidation stabilizers, heat stabilizers, light stabilizers, lubricants, mold release agents, dyes, pigments, and plasticizers. The shaped articles made by injection molding have excellent tensile properties, flexural properties and impact properties. The fibers and films also have excellent mechanical properties, making them useful in applications where high strength is needed. This invention is further illustrated by the following non-limiting examples. Example 1 In a 2 liter glass tubular reactor immersed in a sand bath, equipped with a Vigreaux column and condenser, nitrogen inlet, thermocouple, and a "C"-shaped 316 stainless steel mechanical stirrer were placed (a) 414 grams (3.0 moles) of 4- hydroxybenzoic acid (HBA), (b) 181.5 grams (0.75 moles) of 4,4'-biphenyldicarboxylic acid (BDA), (c) 41.5 grams (0.25 moles) of terephthalic acid (TA), (d) 139.5 grams (0.75 moles) of 4,4'-dihydroxybiphenyl (BP), (e) 37.8 grams (0.25 moles) of 4- hydroxyacetanilide (APAP), (f) 0.108 grams of potassium acetate and (g) 502.1 grams of acetic anhydride (99% purity, 4.87 moles) under a constant purge of nitrogen (30-40 cc/min). The reactor was heated in stages using a MicRIcon® control unit to run the following temperature profile: (1) 1 minute at 25 °C; (2) 50 minutes to 125 °C; (3) 40 minutes to 140°C; (4) 20 minutes to 150°C; (5) 45 minutes to 200°C; (6) 5 minutes to 210°C; (7) 6 minutes to 220°; (8) 50 minutes to 275°C; (9) 80 minutes to 310°C; (10) 25 minutes to 335°C; (11) 25 minutes to 360°C; (12) 15 minutes at 360°C; and (13) 120 minutes at 360°C. In the above temperature profile, steps 1, 12 and 13 are isothermal. In the other steps, the temperature was raised from the temperature at the end of the previous step to the new specified temperature during the specified time. The reaction mixture was kept under nitrogen flow until the end of step 12 of the temperature profile above. At this time, 96-98% of the theoretical yield of acetic acid had been collected. The nitrogen was then turned off and the reactor was evacuated to about 30 mbar over a period of 30 minutes. During this time the torque of the stirrer started to rise. The reaction was stopped when the increase in torque required an increase of 30 mV to the stirrer. The reactor was then cooled to room temperature and broken to obtain the polymer. The polymer was cut into small cubes and ground. The polymer had an inherent viscosity (I.V.) of 6.97 dl/g when measured in a mixture of pentafluorophenol (50 vol.%) and hexafluoroisopropanol (50 vol.%) at a concentration of 0.1% (w/v) and at a temperature of 25 °C. The melting temperature (T , heat of melting (ΔH-J, crystallization temperature on cooling from the molten state (TJ, and heat of crystallization (ΔHJ were found to be 315°C, 2.4 joules/gram, 270°C, and -2.3 joules/gram respectively as determined by differential scanning calorimetry (DSC; 20°C/min heating rate). The melt viscosity of the polymer, measured in a capillary viscometer at 360 °C at a shear rate of 1000 sec "1 , was 320 poise. These properties are summarized in Table 1. The molten polymer was extruded at 350 °C through a single hole spinneret (0.005 inch diameter and 0.007 inch length) at a rate of 0.45 g/min. The extruded filament was drawn down at a speed of 800 meters/minute and quenched in air at ambient conditions (ca. 25 °C and 65% relative humidity). The tensile properties of the as-spun fiber were measured using ASTM test method D-3822: tenacity, 7.7 gms per denier (gpd); modulus, 540 gpd; elongation at break, 1.5%. The fiber was heat treated in an unstressed state at 300°C for 8 hours under nitrogen. The resulting tensile properties were: tenacity, 14.7 gpd; modulus, 630 gpd; elongation, 2.1%. Examples 2-12 Other polymers were synthesized, processed and tested using substantially the same conditions as in example 1, with the exception of the monomer ratios of terephthalic acid, 4,4'-dihydroxybiphenyl and 4-hydroxyacetanilide. The amount of acetic anhydride needed for the acetylation was also adjusted accordingly. Most experiments were carried out on a 5-mole scale, but Example 12 was carried out on a larger scale (4 liter flask, 10 moles), where the amounts of monomer and chemicals were doubled and the same temperature profile was used. The compositions and physical properties of the polymers are summarized in Table 1. Polymers of the same composition obtained from duplicate runs in Examples 1-2, 3-4, 5-6, 7-8, and 9-10 were combined, compounded with 30 weight % glass fiber, and injection molded into test specimens for the evaluation of their tensile properties (ASTM D638), flexural properties (ASTM D790), notched Izod (ASTM D256), and heat deflection temperatures (ASTM D648). The test specimens were injection molded at a barrel temperature in the range of 330-360°C and a mold temperature of 100°C. The test results are summarized in Table 2. The polymers in Examples 2-12 were extruded into single filament fibers as described for Example 1. The spinning temperatures ranged from 330-370°C. The fibers were then tested and heat treated under the conditions described for Example 1. The properties of the as-spun and heat-treated fibers are summarized in Table 3. Comparative Examples C-l and C-2 Using essentially the method described in Example 1 , a polymer was made from 414 grams (3.0 moles) of 4-hydroxybenzoic acid (HBA), 181.5 grams (0.75 moles) of 4,4'-biphenyldicarboxylic acid (BDA), 41.5 grams (0.25 moles) of terephthalic acid (TA), 186 grams (1.0 moles) of 4,4'-dihydroxybiphenyl (BP), 0.1 11 grams of potassium acetate and 528.5 grams (99% purity, 5.0 moles) of acetic anhydride. The inherent viscosity of the polymer was not measured as it was insoluble in a mixture of pentafluorophenol (50 vol.%) and hexafluoroisopropanol (50 vol.%). The melting temperature (T , heat of melting (ΔH m ), crystallization temperature on cooling from the molten state (T c ), and heat of crystallization (ΔH C ) were measured by differential scanning calorimetry (DSC; 20°C/min heating rate). The melt viscosity of the polymer was measured in a capillary viscometer at 360 °C at a shear rate of 1000 sec " '. The properties are summarized in Table 1. The polymer samples of Comparative Examples C-l and C-2 were combined, compounded with 30% glass fiber, and injection molded into test specimens as described in Examples 1-10. The mechanical properties are summarized in Table 2. The polymer samples were also melt spun and heat treated using the method of Example 1. The tensile properties of the as-spun and heat-treated fiber are presented in Table 3. Comparative Example C-3 A larger batch of polymer was made in a 4 liter flask under the conditions described in Example 1 but using twice the amounts of reactants described in Comparative Examples C-l and C-2. Fiber samples were made as described previously. The polymer batch was compounded with 30% glass and made into test specimens for the testing of mechanical properties. The results are summarized in Tables 1, 2 and 3. Table 1. Polymer Compositions/Properties Monomer (Mole %) I.V. 2 Melt Enthalpy (J/g) dl/g Viscosity' Tm 3 Tc 4 Ex. HBA BDA BP TA APAP (poise) CO co ΔHm 3 ΔHc 4 1 60 15 15 5 5 6.97 310 315 270 2.4 -2.3 2 60 15 15 5 5 7.85 370 319 270 1.5 -2.2 3 60 15 18 5 2 8.21 400 325 276 1.5 -2.7 4 60 15 18 5 2 7.95 340 328 274 3.2 -2.3 5 60 15 10 5 10 6.3 370 336 278 2.0 -1.3 6 60 15 10 5 10 5.9 330 340 277 1.7 -1.3 7 60 20 15 _ 5 6.39 460 335 282 3.6 -2.4 8 60 20 15 . 5 6.55 230 334 281 3.7 -1.8 9 60 5 15 15 5 6.54 330 357 297 4.5 -3.9 10 60 5 15 15 5 7.2 270 351 295 4.0 -2.0 11 60 3 15 17 5 5.35 400 361 311 3.4 -2.3 12 60 3 15 17 5 5.34 610 366 308 3.6 -2.9 C-l 5 60 15 20 5 - insol. 520 338 283 1.4 -1.5 C-2 5 60 15 20 5 _ insol. 300 338 290 2.8 -1.4 C-3 5 60 15 20 5 - 6.75 220 334 287 5.3 -1.9 1. Melt viscosity at 360° C and 1000 sec-1. 2. Inherent viscosity in 50:50 (v/v) pentafluorophenol and hexafluoroisopropanol at 25 °C at a conce of 0.1% (w/v). 3. Measured by DSC at a heating rate of 20°C/min. 4. Measured by DSC on cooling from the melt. (Negative means heat is released). 5. C-l - C-3 are Comparative Examples Table 2: Mechanical properties of glass filled polymers (30% glass fiber) HDT Tensile Properties Flexural Properties (@ 264 Modulus Strength Notched psi) Elongation (Mpsi) (Kpsi) Modulus Strength Izod Example (°C) (%) (Mpsi) (Kpsi) (ft-lb/in.) 1+2 265 2.48 23.72 1.82 2.17 30.1 3.23 3+4 260 1.89 18.8 2.1 1.76 25.1 2.52 5+6 266 3.24 28.1 1.65 2.46 32.2 3.53 7+8 279 2.13 21.02 2.03 2.06 28.9 2.72 9+10 284 2.16 21 1.9 2.1 29 3.37 11+12 280 2.72 24.45 1.92 2.21 27.4 3.36 Comparative Examples C-l + C-2 278 2.23 21.71 1.78 2.03 28.44 2.7 C-3 267 1.9 19.1 2 1.6 25.7 2.1 Table 3: Fiber Properties As Spun Heat Treated Example Tenacity Elongation Modulus Tenacity Elongation Modulus (gpd) (%) (gpd) (gpd) (%) (gpd) 1 7.7 1.5 540 14.7 2.1 630 2 8.2 1.6 560 15.9 2.1 690 3 8.2 1.8 540 20.3 2.3 820 4 8 1.6 610 14.4 1.7 810 5 9.3 1.7 680 16.5 1.9 830 6 7.2 1.6 530 16.6 0.8 730 7 8.3 1.6 575 NM 1 NM' NM 1 8 6.9 1.3 610 17.7 2.4 750 9 8.5 1.8 540 21 2 1000 10 8.3 1.8 560 23.3 2.2 990 11 6.8 1.4 540 24 2.3 950 12 6.6 1.3 550 23.4 2.8 880 Comparative Examples C-l 3.6 1 430 5.6 0.9 630 C-2 6.7 1.3 540 13.7 1.7 730 C-3 6.4 1.3 540 16.4 1.7 930 1. Not Measured. Example 13 Using essentially the same procedure as in Example 1, a polymer was made on a 5-mole scale from 4-hydroxybenzoic acid (60 mole %), 4,4'-biphenyldicarboxylic acid (18.25 mole %), 4,4'-dihydroxybiphenyl (13.25 mole %), 4-hydroxyacetanilide (5 mole %), and 6-hydroxy-2-naphthoic acid (3.5 mole %). The polymer had an inherent viscosity of 7.3 dl/g and a elt viscosity of 430 poise when measured at 360°C and 1000 sec- 1 . The thermal properties as measured by DSC were: T m , 302°C; Tc, 255°C; enthalpy of melting, 3 J/g; and enthalpy of crystallization, -2.2 J/g. The polymer was melt spun into a single filament fiber as described in Example 1. The tensile properties of the as-spun fiber were: tenacity, 6.7 gpd; modulus, 550 gpd; elongation at break, 1.3%. The fiber was then heat treated by the method described in Example 1, and its tensile properties were again measured: tenacity, 14 gpd; modulus, 865 gpd; elongation at break, 1.6%. Example 14 A duplicate batch of the polymer of Example 13 was made using essentially the same method but on a 10-mole scale. This batch of polymer had an inherent viscosity of 6.6 dl/g and a melt viscosity of 400 poise at 360°C and 1000 sec-1. The thermal properties as measured by DSC were: T m , 296°C; Tc, 246°C; enthalpy of melting, 1.8 J/g; and enthalpy of crystallization, -1.6 J/g. The polymer was melt spun into a single filament fiber having the following as-spun properties: tenacity, 5.0 gpd; modulus, 500 gpd; elongation, 1.1%. The two batches of Examples 13 and 14 were then combined and compounded with glass fiber to produce a 30% glass-filled polymer. This was injection molded into test specimens which had the following properties: heat distortion temperature (264 psi load), 238°C; tensile modulus, 2.72 Mpsi; tensile strength, 19.98 Kpsi; elongation, 2.06%; flexural modulus, 2.07 Mpsi; flexural strength, 29.3 Kpsi; notched Izod, 1.93 ft- lb/in. Example 15 A polymer was prepared using the same method as in Example 1, using as monomers 4-hydroxybenzoic acid (60 mole %), 4,4'-biphenyldicarboxylic acid (15 mole %), terephthalic acid (5 mole %), 1,4-hydroquinone (15 mole %) and 4- hydroxyacetanilide (5 mole %). The reaction mixture solidified as polymerization proceeded rather than yielding a molten polymer and was discarded. It is to be understood that the above described embodiments of the invention are illustrative only and that modification throughout may occur to one skilled in the art. Accordingly, this invention is not to be regarded as limited to the embodiments disclosed herein.

Claims: CLAIMS We Claim: 1. A thermotropic aromatic poly(esteramide) comprising monomer units A, B, C and D, where A is and optionally the dioyl residue of one or more aromatic diacids; B is the dioxy residue of one or more aromatic diols; C is 4-oxybenzoyl, 6-oxy-2-naphthoyl, or a mixture thereof; D is one or more monomer units selected from the group consisting of where R and R are alike or different and are selected from the group consisting of H, C, to C 4 alkyl, and phenyl, said C, to C 4 alkyl optionally being substituted with Cl, F and mixtures thereof, said phenyl being optionally substituted with Cl, F, C, to C 4 alkyl, and mixtures thereof; wherein some or all of the aromatic groups of said monomer units A, B, C, and D are optionally substituted with one or more moieties selected from the group consisting of F, Cl, Br, I, and C, to C 4 alkyl groups that may be partially or fully substituted with Cl, F, and mixtures thereof; wherein said poly(esteramide) comprises on a molar basis about 1 to about 45% of said monomer unit A, about 1 to about 45% of said monomer unit B, about 10 to about 95% of said monomer unit C, and about 1 to about 30% of said monomer unit D; wherein said poly(esteramide) is capable of forming a liquid crystalline melt at a temperature greater than or equal to about 200 °C and less than or equal to about 400 °C. 2. A thermotropic aromatic poly(esteramide) as recited in Claim 1, wherein said monomer unit A is and one or more optional dioyl residues of aromatic diacids selected from the group consisting of terephthalic acid, isophthalic acid, 2,6- naphthalenedicarboxylic acid, and 2,7-naphthalenedicarboxylic acid; and said monomer unit B is the dioxy residue of one or more aromatic diols selected from the group consisting of 1 ,4-hydroquinone, 4,4'-biphenol, 2,6- dihydroxynaphthalene, and 2,7-dihydroxynaphthalene. The thermotropic poly( esteramide) as recited in Claim 2, wherein said monomer unit D is 4. The thermotropic aromatic poly(esteramide) as recited in Claim 3, wherein said monomer unit C comprises said 4-oxybenzoyl and 0 to about 15% of said 6-oxy- 2-naphthoyl, expressed as a mole % of the monomer units of said poly(esteramide). 5. The thermotropic aromatic poly(esteramide) as recited in Claim 4, said poly(esteramide) comprising on a molar basis about 3 to about 30% of said monomer unit A, about 3 to about 30% of said monomer unit B, about 40 to about 90% of said monomer unit C, and about 1 to about 20% of said monomer unit D. 6. The thermotropic aromatic poly(esteramide) as recited in Claim 4, said poly(esteramide) comprising on a molar basis about 10 to about 30% of said monomer unit A, about 5 to about 25% of said monomer unit B, about 50 to about 80% of said monomer unit C, and about 5 to about 15% of said monomer unit D. 7. The thermotropic aromatic poly(esteramide) as recited in Claim 5, wherein said poly(esteramide) is capable of forming a liquid crystalline melt at a temperature of at least about 250°C and less than or equal to about 375 °C. 8. The thermotropic aromatic poly(esteramide), as recited in Claim 6, wherein said monomer unit A is comprised of and optional terephthaloyl, said terephthaloyl comprising up to about 25 mole % of the monomer units of said poly(esteramide); and wherein said monomer unit B is comprised of the dioxy residue of 4,4'-biphenol and optional 1 ,4-hydroquinone, said dioxy residue of 1,4-hydroquinone comprising up to about 20 mole % of the monomer units of said poly(esteramide). The thermotropic aromatic poly(esteramide) as recited in Claim 6, wherein said monomer unit A comprises about 2 to about 25% of and about 2 to about 25% of terephthaloyl, expressed as a mole % of the monomer units of said poly(esteramide); wherein said monomer unit B is the dioxy residue of 4,4'-biphenol; and wherein said monomer unit C is 4-oxybenzoyl. 10. The thermotropic aromatic poly(esteramide) as recited in Claim 6, wherein said monomer unit A is wherein said monomer unit B is the dioxy residue of 4,4'-biphenol; and wherein said monomer unit C comprises about 35 to about 78% of said oxyaroyl residue of 4-hydroxybenzoic acid and about 2 to about 15% of said oxyaroyl residue of 6-hydroxy-2-naphthoic acid, expressed as a mole % of the monomer units of said poly(esteramide). 11. A shaped article comprising the thermotropic aromatic poly(esteramide) recited in Claim 1. 12. A fiber comprising the thermotropic aromatic poly(esteramide) recited in Claim 1. 13. A shaped article comprising the thermotropic aromatic poly(esteramide) recited in Claim 8. 14. A fiber comprising the thermotropic aromatic poly(esteramide) recited in Claim 8. 15. A composition suitable for injection molding comprising the thermotropic aromatic poly(esteramide) recited in Claim 1, and up to about 70% by weight of one or more additives. 16. The composition of Claim 15, comprising one or more additives selected from the group consisting of glass fiber, calcium silicate, silica, clays, talc, mica, polytetrafluoroethylene, graphite, alumina trihydrate, sodium aluminum carbonate, barium ferrite, wollastonite, carbon fiber, polymeric fiber, aluminum silicate fiber, titanium fiber, rock wool fiber, steel fiber, tungsten fiber, and wollastonite fiber. 17. A composition suitable for injection molding comprising the thermotropic aromatic poly( esteramide) recited in Claim 8 and up to about 70% by weight of one or more additives. 18. The composition of Claim 17, comprising one or more additives selected from the group consisting of glass fiber, calcium silicate, silica, clays, talc, mica, polytetrafluoroethylene, graphite, alumina trihydrate, sodium aluminum carbonate, barium ferrite, wollastonite, carbon fiber, polymeric fiber, aluminum silicate fiber, titanium fiber, rock wool fiber, steel fiber, tungsten fiber, and wollastonite fiber. 19. A method of synthesizing a thermotropic aromatic poly(esteramide) which forms a liquid crystalline melt at a temperature of at least about 200°C and less than or equal to about 400°C, comprising, the step of condensing on a mole basis about 1 to about 45% of monomer A, about 1 to about 45% of monomer B, about 10 to about 95%) of monomer C, and about 1 to about 30%) of monomer D, or reactive derivatives of said monomers A, B, C and D, where A is and optionally one or more aromatic diacids selected from the group consisting of terephthalic acid, isophthalic acid, 2,6-naphthalenedicarboxylic acid, and 2,7- naphthalenedicarboxylic acid; B is one or more aromatic diols selected from the group consisting of 1,4- hydroquinone, 4,4'-biphenol, 2,6-dihydroxynaphthalene, and 2,7- dihydroxynaphthalene; C is 4-hydroxybenzoic acid, 6-hydroxy-2-naphthoic acid, or a mixture thereof; and D is one or more monomer units selected from the group consisting of where R and R are alike or different and are selected from the group consisting of H, C, to C 4 alkyl and phenyl, said C, to C 4 alkyl optionally being substituted with Cl, F, and mixtures thereof, said phenyl being optionally substituted with Cl, F, C, to C 4 alkyl, and mixtures thereof; wherein some or all of the aromatic groups of said monomer units A, B, C, and D are optionally substituted with F, Cl, Br, I, and C, to C 4 alkyl groups that may be partially or fully substituted with Cl, F, and mixtures thereof; wherein said monomers A, B, C and D are condensed to yield a poly(esteramide) having an inherent viscosity of at least about 5dl/g when measured at about 25 °C as a 0.1% solution on a weight/volume basis in a mixture of equal volumes of pentafluorophenol and hexafluoroisopropanol. 20. The method of synthesizing a thermotropic aromatic poly(esteramide) as recited in Claim 19, comprising the step of condensing on a mole basis about 3 to about 30% of monomer A, about 3 to about 30% of monomer B, about 40 to about 90% of monomer C, and about 1 to about 20% of monomer D, including reactive derivatives of said monomers A, B, C and D, wherein said monomer C comprises 4-hydroxybenzoic acid and 0 to about 15% of 6-hydroxy-2-naphthoic acid or reactive derivatives thereof, expressed as a mole % of all the reacting monomers, and wherein said monomer D is 4-aminophenol or a reactive derivative thereof. 21. The method of synthesizing a thermotropic aromatic poly(esteramide) as recited in Claim 20, comprising the step of condensing on a mole basis about 10 to about 30% of monomer A, about 5 to about 25% of monomer B, about 50 to about 80% of monomer C, and about 5 to about 15% of monomer D, including reactive derivatives of said monomers A, B, C, and D. 22. The method of synthesizing a thermotropic aromatic poly(esteramide) from said monomers A, B, C, and D, or reactive derivatives thereof, as recited in Claim 21, wherein said monomer A is and 0 to about 25% of terephthalic acid, measured as a mole % of the composition; and wherein said monomer B is 4,4'-biphenol and 0 to about 20% of 1,4- hydroquinone, measured as a mole % of the composition. 23. The method of synthesizing a thermotropic aromatic poly(esteramide) as recited in Claim 22, wherein said monomer A comprises about 2 to about 25% of and about 2 to about 25% of terephthalic acid, expressed as a mole % of all of the monomers; wherein said monomer B is 4,4'-biphenol; and wherein said monomer C is 4-hydroxybenzoic acid; including reactive derivatives of said monomers A, B, and C. 24. The method of synthesizing a thermotropic aromatic poly(esteramide) as recited in Claim 22, wherein said monomer A is said monomer B is 4,4'-biphenol, and said monomer C comprises about 35 to about 78% 4-hydroxybenzoic acid and about 2 to about 15% of 6-hydroxy-2- naphthoic acid, expressed as a mole % of all the monomers, including reactive derivatives of said monomers A, B and C.

Inventors: GUPTA BALARAM, HATKE WILFRIED, SAWYER LINDA C, SHEPHERD JAMES P, GUPTA, BALARAM, HATKE, WILFRIED, SAWYER, LINDA, C., SHEPHERD, JAMES, P.
Applicants: HOECHST CELANESE CORP, HOECHST CELANESE CORPORATION
Application year: 1994
Main classification: C08G63
IPC codes: C08G69, C08K3, C08K7, C08L77, D01F6